US11522220B2 - Electrolyte composition - Google Patents

Electrolyte composition Download PDF

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US11522220B2
US11522220B2 US16/649,753 US201816649753A US11522220B2 US 11522220 B2 US11522220 B2 US 11522220B2 US 201816649753 A US201816649753 A US 201816649753A US 11522220 B2 US11522220 B2 US 11522220B2
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electrolyte composition
ionic
block
imtfsi
organic
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US20200280095A1 (en
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John Chiefari
Kristine Barlow
Nicolas Goujon
Xiaojuan Hao
Maria Forsyth
Patrick C. Howlett
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Commonwealth Scientific and Industrial Research Organization CSIRO
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    • H—ELECTRICITY
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    • H01M8/1041—Polymer electrolyte composites, mixtures or blends
    • H01M8/1046—Mixtures of at least one polymer and at least one additive
    • H01M8/1048—Ion-conducting additives, e.g. ion-conducting particles, heteropolyacids, metal phosphate or polybenzimidazole with phosphoric acid
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    • H01M4/485—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of mixed oxides or hydroxides for inserting or intercalating light metals, e.g. LiTi2O4 or LiTi2OxFy
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Definitions

  • the present invention relates to electrolyte compositions, and in particular to block copolymer electrolyte compositions and devices comprising the same.
  • Solid-state polymer electrolytes are a promising substitute to liquid electrolytes for the fabrication of high performance ion conducting electrolytes, and in particular high-performance lithium-ion conducting electrolytes.
  • Polymer electrolytes promise an improvement of the overall electrochemical performance and safety of lithium-based devices due to their good shape flexibility, suppression of dendrite growth, removal of leakage issues and lower flammability relative to liquid electrolytes.
  • Block copolymer electrolytes form part of a particular class of polymer electrolytes that have recently attracted attention due to their highly customisable chemical nature.
  • polymer electrolytes prepared to date have generally been found to be defective in either ionic conductivity and/or mechanical stability. Poor ionic conductivity leads to the production of solid-state devices that suffer from low storage capacity, energy and power.
  • poor mechanical stability adversely affects the electrochemical stability and/or cycleability of the electrolyte.
  • block copolymer electrolytes that can provide ionic conductivities comparable to those of their liquid counterparts, as well as sufficiently good mechanical properties to ensure electrochemical stability and cycleability.
  • the present invention relates to electrolyte compositions obtained by combining a block copolymer, an organic electrolyte, and a lithium salt. It has surprisingly been observed that by controlling the glass transition temperature (Tg) profile of the electrolyte composition it is possible to provide solid-state electrolytes having high electrochemical and mechanical stability. This may be achieved, for example, by tuning a number of chemical and physical parameters of the composition which include the molar weight of the copolymer, the amount of lithium contained in the electrolyte composition, and the amount and type of the organic electrolyte.
  • Tg glass transition temperature
  • the present invention provides an electrolyte composition
  • a block copolymer comprising (i) a block copolymer, (ii) an organic electrolyte, and (iii) a lithium salt
  • the block copolymer comprises a non-ionic block and an ionic block, the non-ionic block comprising polymerised residues of hydrophobic monomers, and the ionic block comprising polymerised monomer residues having covalently coupled thereto (a) a pendant organic ionic liquid cation, the pendant organic ionic liquid cation having a counter anion, (b) a pendant anionic moiety, the pendant anionic moiety having a counter cation, or (c) a combination thereof, and wherein the electrolyte composition has at least two glass transition temperature (Tg) values.
  • Tg glass transition temperature
  • the at least two Tg values of the electrolyte composition is characteristic of its morphology having micro-phase separation. Without wanting to be confined by theory, such morphology is believed to be beneficial to both the ionic conductivity and the mechanical properties of the composition. For example, it is believed an electrolyte composition morphology characterised by micro-phase separation ensures preferential pathways for ionic diffusion, thus promoting ionic conductivity. On the other hand, it is believed that such micro-phase separation emphasises the composite-like character of the composition, thus improving its overall mechanical properties. It was surprising to observe multiple glass transition temperatures characteristic after the addition of an organic electrolyte (e.g. an ionic liquid), the counter ions and lithium salt to the block copolymer, since these types of additions traditionally have caused block copolymers to plasticise.
  • an organic electrolyte e.g. an ionic liquid
  • the electrolyte of the present invention can present as a solid at nominal operational conditions of an electrochemical device.
  • the composition may present as a solid at least at room temperature, for example at about 20° C.
  • the electrolyte composition presenting “as a solid” the composition is characterised by sufficient structural rigidity to support its own weight and maintain its shape in the absence of external factors such as constrictions (e.g. a container) or applied forces.
  • the electrolyte composition presents as a solid at least at about 30° C., about 50° C., about 70° C., or about 80° C.
  • the electrolyte composition may present as a solid at a temperature up to 100° C.
  • the molar weight of the non-ionic block combined with the ionic block is less than 40,000 g/mol.
  • copolymers in which the molar weight of the non-ionic block combined with the ionic block is less than 40,000 g/mol offer a particularly advantageous balance between ionic conductivity and mechanical stability. Without wanting to be confined by theory, it is believed that such a range of molar weights assists with the compactness of the overall polymer structure, at the same time reducing resistance to ionic diffusion.
  • the lithium salt is present in an amount of at least 11 wt. % relative to the total weight of the electrolyte composition.
  • a content of at least 11% weight percent of lithium salt in the electrolyte composition assists with both high ionic conductivity and mechanical stability.
  • the organic electrolyte is present in an amount of less than 55 wt. % relative to the total weight of the electrolyte composition.
  • an amount of organic electrolyte of less than 55.0 wt. % relative to the total weight of the electrolyte composition reduces adverse plasticising effects and/or assists in providing an advantageous balance between high ionic conductivity and mechanical stability of the electrolyte composition.
  • the organic electrolyte is an organic ionic liquid having a cation and a counter anion, the organic ionic liquid not being covalently coupled to the block copolymer.
  • the present invention also provides an electrolyte composition
  • an electrolyte composition comprising (i) a block copolymer, (ii) an organic ionic liquid having a cation and a counter anion, the organic ionic liquid not being covalently coupled to the block copolymer, and (iii) a lithium salt
  • the block copolymer comprises a non-ionic block and an ionic block, the non-ionic block comprising polymerised residues of hydrophobic monomers, and the ionic block comprising polymerised monomer residues having covalently coupled thereto (a) a pendant organic ionic liquid cation, the pendant organic ionic liquid cation having a counter anion, (b) a pendant anionic moiety, the pendant anionic moiety having a counter cation, or (c) a combination thereof, and wherein the electrolyte composition has at least two glass transition temperature (Tg) values.
  • Tg glass transition temperature
  • the organic ionic liquid not covalently coupled to the block copolymer may herein be referred to as “uncoupled ionic liquid” or “free ionic liquid”.
  • the organic ionic liquid not covalently coupled to the block copolymer may be present in an amount of less than 55 wt. % relative to the total weight of the electrolyte composition.
  • an amount of uncoupled ionic liquid of less than 55.0 wt. % relative to the total weight of the electrolyte composition reduces adverse plasticising effects and/or assists in providing an advantageous balance between high ionic conductivity and mechanical stability of the electrolyte composition.
  • the cation of the organic liquid that is not covalently coupled to the block copolymer is selected from an ammonium cation, a pyridinium cation, a pyrrolidinium cation, a phosphonium cation, and a combination thereof. It was surprisingly observed the choice of the cation selected from an ammonium cation, a pyridinium cation, phosphonium cation, a pyrrolidinium cation, and a combination thereof promotes formation of particularly stable Solid-Electrolyte Interface (SEI) on the surface of an electrode. That advantageously assists with the cycleability of a device comprising the electrode since the tendency to form dendrites is reduced, in turn increasing the safety characteristics of the device.
  • SEI Solid-Electrolyte Interface
  • the electrolyte composition according to the invention has at least two glass transition temperature (Tg) values as measured by Differential Scanning Calorimetry (DSC), and may also have one or more features selected from:
  • the present invention also provides a lithium-based electrochemical cell comprising a negative electrode and an electrolyte composition as described herein.
  • FIG. 1 shows the molecular structure of an electrolyte composition
  • FIG. 2 shows ionic conductivity values for S-ImTFSI (64-16) block copolymers with various Li cat /poly cat molar ratio and a fixed IL cat /poly cat molar ratio of 0.39 as well as S-ImTFSI (64-16), at a temperature range of ⁇ 100 to 100° C.;
  • FIG. 3 Small Angle X-ray Scattering (SAXS) profiles at room temperature of the S-ImTFSI block copolymers with different styrene DP and PIL DP, with and without annealing treatment;
  • FIG. 4 shows SAXS profiles of the S-ImTFSI (64-16) with various Li cat /poly cat molar ratio (i.e. 0.00, 0.58, 3.00 and 5.81) and a fixed IL cat /poly cat molar ratio of 0.39 as well as S-ImTFSI (64-16), without (A) and (B) with annealing treatment at 120° C. for 24 hours;
  • FIG. 5 shows SAXS profiles of the S-ImTFSI compositions having a poly cat :Li cat :IL cat molar ratio of 1:00:5.81:0.39, with different styrene and PIL degree of polymerization;
  • FIG. 6 shows galvanostatic cycling at 50° C. of S-ImTFSI (64-16) compositions having various Li cat /poly cat molar ratio (specifically (a) 0.58, (b) 3.00 and (c) 5.81) at a fixed IL cat /poly cat molar ratio of 0.39, from a current density of 0.02 mA ⁇ cm ⁇ 2 to 0.2 mA ⁇ cm ⁇ 2
  • FIG. 7 shows galvanostatic cycling at 50° C. of S-ImTFSI (127-31) with a poly cat :Li cat :IL cat molar ratio of 1:00:5.81:0.39, from a current density of 0.02 mA ⁇ cm ⁇ 2 to 0.2 mA.cm ⁇ 2 ;
  • FIG. 9 shows (a) the synthesis scheme of styTFSI.Et 3 NH monomer, and (b) the synthesis scheme of mTFSI.Et 3 NH monomer, in the presence of BHT inhibitor,
  • FIG. 10 shows the synthesis scheme of lithium poly(methylmethacrylate-b-4-styrenesulfonyl(trifluoromethylsulfonyl)imide) (MA-sTFSILi) (116-29) copolymer,
  • FIG. 11 shows the synthesis schematic of poly(methylmethacrylate-b-1-[3-(methacryloyloxy)-propylsulfonyl]-1-(trifluoromethylsulfonyl)imide) (MA-mTFSILi) (116-29) copolymer,
  • FIG. 12 shows the synthesis schematic of a copolymer having a PMMA-based non-ionic block and an butyl-imidazolium-based ionic block
  • FIG. 13 shows DSC data for (a) a PMMA-ImTFSI (116-32) block co-polymer having a (poly cat :Li cat :IL cat ) molar ratio of 1:00:5.81:0.39, and (b) an electrolyte composition obtained combining the PMMA-ImTFSI (116-32) block co-polymer with a lithium salt and an organic ionic liquid,
  • FIG. 14 shows the synthesis schematic of a poly-styrene(S)-based copolymer having an ionic block comprising a styrene-TFSI (sTFSI) anionic pendant moiety,
  • sTFSI styrene-TFSI
  • FIG. 15 shows DSC data obtained on four electrolyte compositions, respectively obtained combining a lithium salt, an organic ionic liquid, and (A) a S-Im/TFSI(64-16) copolymer, (B)S-Im/TFSI(64-16) and S-sTFSI/Li(64-17) copolymers used at a 1/1 molar ratio, (C)S-Im/TFSI(64-16) and S-sTFSI/Li(64-17) copolymers used at a 1/2 molar ratio, or (D) a S-sTFSI/Li(64-17) copolymer,
  • FIG. 16 shows ionic conductivity values measured on four electrolyte compositions, respectively obtained combining a lithium salt, an organic ionic liquid, and (A) a S-Im/TFSI(64-16) copolymer, (B)S-Im/TFSI(64-16) and S-sTFSI/Li(64-17) copolymers used at a 1/1 molar ratio, (C)S-Im/TFSI(64-16) and S-sTFSI/Li(64-17) copolymers used at a 1/2 molar ratio, or (D) a S-sTFSI/Li(64-17) copolymer,
  • Li-TFSI lithium salt
  • Li:copolymer organic electrolyte
  • EC:copolymer ethylene carbonate
  • the electrolyte composition of the present invention comprises a block copolymer.
  • block copolymer is meant a polymer chain that comprises (i) polymerised monomer residues that provide for a non-ionic block, and (ii) polymerised monomer residues that provide for an ionic block.
  • the block copolymer may be an AB di-block linear copolymer, where A represents a non-ionic block and B represents an ionic block.
  • the block copolymer may comprise more than two blocks.
  • the block copolymer may be a tri-block copolymer.
  • the block copolymer only comprises a non-ionic block and an ionic block.
  • the block copolymer of the present invention comprises a non-ionic block.
  • non-ionic block is meant a polymer block that does not contain ionic charge.
  • the non-ionic block is a neutral polymer block.
  • the non-ionic block comprises polymerised residues of hydrophobic monomers.
  • hydrophobic monomers is meant monomers that when homo-polymerised or co-polymerised with each other form polymer that is substantially insoluble in water.
  • the residues of hydrophobic monomers may be derived from acrylate monomer, vinyl monomer, styrenic monomer, or combinations thereof.
  • the non-ionic block may be described as a hydrophobic non-ionic block.
  • the residues of hydrophobic monomers are derived from styrene or styrene derivatives, indene or indene derivatives, vinylpyridine or vinylpyridine derivatives, methyl methacrylate or methacrylate derivatives, or a combination thereof.
  • residues of hydrophobic monomers may be derived from ⁇ -methylstyrene, methylstyrene, chlorostyrene, hydroxystyrene, vinylbenzyl chloride, methylindene, ethylindene, trimethylindene, vinylmethylpyridine, vinylbutylpyridine, vinylquinioline, vinylacrydine, hydroxyethyl methacrylate, dimethylamino-ethyl methacrylate, vinylcarbazole, or a combination thereof.
  • the residues of hydrophobic monomers are derived from styrene.
  • the non-ionic block comprises a repeating unit having either of the following structures (I) and (II):
  • R 1 , R 2 , R 3 , and R 4 are each independently H or C 1-6 alkyl.
  • R 1 and R 2 may both be H
  • both R 3 and R 4 may be C 1-3 alkyl
  • R 1 and R 2 may be both H and R 3 and R 4 may be both methyl.
  • the molar weight of the non-ionic block combined with the ionic block of the copolymer is less than 40,000 g/mol.
  • the block copolymer of the electrolyte composition of present invention also comprises an ionic block.
  • ionic block is meant a polymer block that contains an overall ionic charge.
  • the monomer residues of the ionic block may derive from styrene or styrene derivatives, indene or indene derivatives, vinylpyridine or vinylpyridine derivatives, methyl methacrylate or methacrylate derivatives, methyl acrylate or acrylate derivatives, methacrylamide or acrylamide derivatives, or a combination thereof.
  • the monomer residues of the ionic block derive from ⁇ -methylstyrene, methylstyrene, chlorostyrene, hydroxystyrene, vinylbenzyl chloride, methylindene, ethylindene, trimethylindene, vinylmethylpyridine, vinylbutylpyridine, vinylquinioline, vinylacrydine, hydroxyethyl methacrylate, dimethylamino-ethyl methacrylate, vinylcarbazole, or a combination thereof.
  • the type of the pendant organic ionic liquid cation is not particularly limited provided it presents as a pendant moiety to the monomer residues forming the backbone of the ionic block.
  • the pendant organic ionic liquid cation comprises any known ionic liquid cation type.
  • the cation may be mono-, di-, or tri-substituted, typically alkyl substituted, where each alkyl independently defined to include C 1-8 linear, branched, or cyclic carbon moieties.
  • the pendant organic ionic liquid cation comprises a carboalkoxy, carboxylato, carboxyamino, alkylene, alkenylene, or ether group linking the cation to the polymerised monomer residues of the ionic block.
  • the ionic block comprises a repeating unit having the following structure (III):
  • R 5 , R 6 , R 7 , and R 8 are each independently H or optionally substituted C 1-12 alkyl, and n has a value in a range from 0 to about 20, or from 0 to about 10, or from 0 to about 5.
  • R 5 and R 6 may be both H
  • R 7 and R 8 may be both C 1-6 alkyl
  • R 5 and R 6 may be both H
  • R 7 may be methyl
  • R 8 may be n-butyl, with n between 1 or about 10.
  • the pendant organic ionic liquid cation comprises 1-butyl(propyl)-1-methylpyrrolidinium (C 4 C 3 mpyr), N-methyl-N-propylpyrrolidinium (C 3 mpyr), N-butyl-N-methylpyrrolidinium (C 4 mPyr), 1-ethyl-3-methylimidazolium (C 2 mim), 1-propyl-3-methylimidazolium (C 3 mim), 1-butyl-3-methylimidazolium (C 4 mim), 1-hexyl-3-methylimidazolium (C 6 mim), 1-octyl-3-methylimidazolium (C 8 mim), 1-dodecyl-3-methylimidazolium (C 12 mim), 1-hexadecyl-3-methylimidazolium (C 16 mim), 1,2-dimethyl-3-butylimidazolium (C 4 (2-C 1 )mim), 1-(3-aminol,
  • polymerised monomer residues of the ionic block derive from monomers that comprise a pendant organic ionic liquid cation of the kind described herein.
  • monomers that comprise a pendant organic ionic liquid cation of the kind described herein.
  • monomers that comprise a polymerizable moiety and a pendant organic ionic liquid cation.
  • examples of such monomers include acryloyl-imidazolium, acryloyl-pyrrolidinium, acryloyl-pyridinium, vinyl-imidazolium, vinyl-pyrrolidinium, vinyl-pyridinium, styrene-imidazolium, styrene-pyrrolidinium, styrene-pyridinium, and a combination thereof.
  • the pendant organic ionic liquid cation has a counter anion. Provided the counter anion neutralizes the charge of the pendant organic ionic liquid cation, there is no limitation as to the nature of that counter anion.
  • the counter anion of the pendant organic ionic liquid cation is selected from alkyl phosphate, biscarbonate, bistriflimide ((i.e., N(SO 2 CF 3 ) 2 )), N(SO 2 C 2 F 5 ) 2 ⁇ , N(SO 2 CF 3 )(SO 2 C 4 F 9 ) ⁇ , carbonate, chlorate, formate, glycolate, perchlorate, hexasubstituted phosphate (including PF 6 ⁇ , PF 3 (CF 3 ) 3 ⁇ , PF 3 (C 2 F 5 ) 3 ⁇ ), tetra-substituted borate (including e.g., BF 4 ⁇ , B(CN) 4 ⁇ , optionally fluorinated C 1-4 alkyl-BF 3 ⁇ (including BF 3 (CH 3 ) ⁇ , BF 3 (CF 3 ) ⁇ , BF 3 (C 2 H 5 ) ⁇ ,
  • the counter anion of the pendant organic ionic liquid cation is selected from bis(trifluoromethanesulfonyl)imide (TFSI), Triflate (OTf), Tetrafluoroborate (BF 4 ), hexafluorophosphate (PF 6 ), and bis(fluorosulfonyl)imide (FSI), fluorosulfonyl-(trifluoromethanesulfonyl)imide (FTFSI), and a combination thereof.
  • TFSI bis(trifluoromethanesulfonyl)imide
  • OTf Triflate
  • BF 4 Tetrafluoroborate
  • PF 6 hexafluorophosphate
  • FSI bis(fluorosulfonyl)imide
  • FTFSI fluorosulfonyl-(trifluoromethanesulfonyl)imide
  • the ionic block may comprise a pendant anionic moiety.
  • the nature of the pendant anionic moiety is not particularly limited provided it presents as a pendant moiety to the monomer residues forming the backbone of the ionic block.
  • the pendant anionic moiety comprises derivatives of bis(trifluoromethanesulfonyl)imide (TFSI), Triflate (OTf), Tetrafluoroborate (BF 4 ), hexafluorophosphate (PF 6 ), and bis(fluorosulfonyl)imide (FSI), fluorosulfonyl-(trifluoromethanesulfonyl)imide (FTFSI) and a combination thereof.
  • TFSI bis(trifluoromethanesulfonyl)imide
  • OTf Triflate
  • BF 4 Tetrafluoroborate
  • PF 6 hexafluorophosphate
  • FSI bis(fluorosulfonyl)imide
  • FTFSI fluorosulfonyl-(trifluoromethanesulfonyl)imide
  • the pendant anionic moiety has a counter cation.
  • the polymerised monomer residues of the ionic block do not have covalently coupled thereto a pendant anionic moiety.
  • the block copolymer used according to the invention may be prepared by any suitable means.
  • the block copolymer is prepared by a process comprising the polymerisation of ethylenically unsaturated monomers.
  • the polymerisation of the ethylenically unsaturated monomers is preferably conducted using a living polymerisation technique.
  • Examples of living polymerisation include ionic polymerisation and controlled radical polymerisation (CRP).
  • Examples of CRP include, but are not limited to, iniferter polymerisation, stable free radical mediated polymerisation (SFRP), atom transfer radical polymerisation (ATRP), and reversible addition fragmentation chain transfer (RAFT) polymerisation.
  • SFRP stable free radical mediated polymerisation
  • ATRP atom transfer radical polymerisation
  • RAFT reversible addition fragmentation chain transfer
  • the block copolymer is formed by polymerising ethylenically unsaturated monomer under the control of a living polymerisation agent, for example a RAFT agent.
  • a living polymerisation agent for example a RAFT agent.
  • RAFT agents suitable for use in accordance with the invention may be obtained commercially, for example see those described in the Sigma Aldrich catalogue (www.sigmaaldrich.com), or Boron Molecular catalogue (www.boronmolecular.com).
  • the electrolyte composition of the present invention also comprises an organic electrolyte.
  • organic electrolyte refers to an organic substance which can conduct electricity by displacement of charged species (e.g. ions).
  • the charged species which may or may not be part of the organic electrolyte, may be cationic and/or anionic species (e.g. ions) either provided in solution with the substance or integral to the chemical structure of the substance (e.g. ionic liquids).
  • the organic electrolyte comprises carbon.
  • the organic electrolyte comprises an organic non-ionic polar compound.
  • the compound being “non-ionic” the chemical structure of the compound does not comprise ionic bonds.
  • the compound being “polar”, the constituting molecules of the compound present asymmetrical charge distribution resulting in positive and negative charge domains. Accordingly, in those instances the organic electrolyte acts as a vehicle for ion diffusion.
  • electrolyte behaviour may derive at least from lithium cations provided by the lithium salt of the electrolyte composition.
  • ionic species provided by the ionic block of the block copolymer may also contribute to the electrolyte functionality of the organic electrolyte.
  • Suitable organic non-ionic polar compounds include linear ethers, cyclic ethers, esters, carbonates, lactones, nitriles, amides, sulfones, sulfolanes, diethylether, dimethoxyethane, tetrahydrofuran, dioxane, dioxolane, methyltetrahydrofuran, methyl formate, ethyl formate, methyl propionate, propylene carbonate, ethylene carbonate, dimethyl carbonate, diethyl carbonate, ethylmethyl carbonate, dibutyl carbonate, butyrolactones, acetonitrile, benzonitrile, nitromethane, nitrobenzene, dimethylformamide, N-methylpyrolidone, dimethylsulfone, tetramethylene sulfone, sulfolane, thiophene, and a combination thereof.
  • the organic electrolyte is an organic ionic liquid. More specifically, in some embodiments the organic electrolyte is an organic ionic liquid not covalently coupled to the block copolymer.
  • the organic ionic liquid being “not covalently coupled to the block copolymer” is meant that the organic ionic liquid is provided in the electrolyte composition as a component that is not attached to the block copolymer by a covalent bond. In other words, that organic ionic liquid is free from the copolymer in the composition.
  • the organic ionic liquid not covalently coupled to the block copolymer has a cation and a counter anion. It was surprisingly observed that the type of the cation of the organic ionic liquid not covalently coupled to the block copolymer is in itself an effective parameter that can be modified to assist with the ionic conductivity of the electrolyte compositions while maintaining their good mechanical stability. In particular, it has been observed that improved properties can result when the cation of the uncoupled organic liquid is selected from an ammonium cation, a pyridinium cation, a pyrrolidinium cation, and a phosphonium cation.
  • Examples of suitable forms of these cations include 1-butyl(propyl)-1-methylpyrrolidinium (C 4 C 3 mpyr), N-methyl-N-propylpyrrolidinium (C 3 mpyr), N-butyl-N-methylpyrrolidinium (C 4 mPyr), N-ethyl-tris(2-(2-methoxyethoxy)ethyl) ethane ammonium (N 2(2o2o1)3 ), Trihexyl(tetradecyl)phosphonium (P 66614 ), Diethyl(methyl)(isobutyl)phosphonium (P 122i4 ), Triisobutyl(methyl)phosphonium (P 1i4i4i4 ), Triethyl(methyl)phosphonium (P 1222 ), Trimethyl(isobutyl)phosphoinum (P 111i4 ), or a combination thereof.
  • the organic ionic liquid not covalently coupled to the block copolymer comprises a counter anion.
  • the counter anion neutralizes the charge of the organic ionic liquid cation, there is no limitation as to the type of the counter anion.
  • the organic ionic liquid not covalently coupled to the block copolymer comprises a counter anion selected from aqueous or anhydrous alkyl phosphate, biscarbonate, bistriflimide ((i.e., N(SO 2 CF 3 ) 2 ⁇ )), N(SO 2 C 2 F 5 ) 2 ⁇ , N(SO 2 CF 3 )(SO 2 C 4 F 9 ) ⁇ , carbonate, chlorate, formate, glycolate, perchlorate, hexasubstituted phosphate (including PF 6 ⁇ , PF 3 (CF 3 ) 3 ⁇ , PF 3 (C 2 F 5 ) 3 ⁇ ); tetra-substituted borate (including e.g., BF 4 ⁇ , B(CN) 4 ⁇ , optionally fluorinated C 1-4 alkyl-BF 3 ⁇ (including BF 3 (CH 3 ) ⁇ , BF 3 (CF 3 )
  • the organic ionic liquid not covalently coupled to the block copolymer comprises a counter anion selected from bis(trifluoromethanesulfonyl)imide (TFSI), Triflate (OTf), Tetrafluoroborate (BF 4 ), hexafluorophosphate (PF 6 ), and bis(fluorosulfonyl)imide (FSI), fluorosulfonyl-(trifluoromethanesulfonyl)imide (FTFSI), and a combination thereof.
  • a counter anion selected from bis(trifluoromethanesulfonyl)imide (TFSI), Triflate (OTf), Tetrafluoroborate (BF 4 ), hexafluorophosphate (PF 6 ), and bis(fluorosulfonyl)imide (FSI), fluorosulfonyl-(trifluoromethanesulfonyl)imide (FTFSI), and a combination thereof.
  • the electrolyte composition of the present invention also comprises a lithium salt.
  • the lithium salt is selected from lithium bis(tri-fluoromethane)sulfonimide (Li-TFSI), lithium (bis(fluorosulfonyl)imide (Li-FSI), lithium fluorosulfonyl-(trifluoromethanesulfonyl) imide (Li-FTFSI), lithium triflate (LiOTf), lithium perchlorate (LiClO 4 ), lithium tetrafluoroborate (LiBF 4 ), lithium hexafluorophosphate (LiPF 6 ), and a combination thereof.
  • Li-TFSI lithium bis(tri-fluoromethane)sulfonimide
  • Li-FSI bis(fluorosulfonyl)imide
  • Li-FTFSI lithium fluorosulfonyl-(trifluoromethanesulfonyl) imide
  • LiOTf lithium triflate
  • LiClO 4 lithium perchlorate
  • LiBF 4 lithium
  • the number of glass transition (Tg) values (as measured by DSC) observed for the electrolyte composition has in itself been found to be an effective parameter that, independently from other parameters described herein, is indicative of the composition mechanical stability and ionic conductivity.
  • Tg glass transition
  • the “Tg” is a temperature value representative of a temperature or temperature range over which an amorphous polymeric composition (or the amorphous regions in a partially crystalline polymeric composition) changes from a relatively hard and brittle state to a relatively viscous or rubbery state.
  • the number of Tg values for a given composition is determined by DSC.
  • DSC digital versatile system
  • a Tg value of a composition may be defined by a stepwise increase of the heat capacity as a function of temperature. Presence of a Tg value is determined by either the onset temperature (i.e. start point or end point) or inflection point (i.e. mid-point). A skilled person would know how to analyse such curve and identify the number of discontinuities corresponding to the number of Tg values.
  • the Tg of the “composition” is intended to mean that obtained by DSC analysis performed on the composition per se (i.e. including the copolymer, lithium salt and the organic electrolyte). It is nevertheless believed the measured Tg of the composition reflects the Tg of the copolymer in that composition.
  • the Tg profile of the composition may however differ from the Tg profile of the copolymer due to possible plasticising effects on the copolymer deriving from the lithium salt and/or the organic electrolyte present in the composition in addition to the copolymer.
  • the electrolyte composition has at least two Tg values.
  • This is a surprising and very favourable characteristic as lithium salt and a organic electrolyte (e.g. an ionic liquid) in the composition have in the past been known to cause a plasticising effect on the copolymer that can thus alter the number of Tg values of the copolymer when measured by DSC.
  • micro-phase separation disappears or diminishes and only a single Tg is measured in many currently made electrolyte compositions.
  • Tg values of the electrolyte composition The presence of at least two Tg values of the electrolyte composition is believed to indicate the morphology of the composition is characterised by strong micro-phase separation, and that such separation is beneficial to both the ionic conductivity and the mechanical properties of the composition. Without wanting to be confined by theory, it is believed strong micro-phase separation provides preferential pathways for ionic diffusion, thus promoting ionic conductivity. On the other hand, it is believed that such separation emphasises the composite-like character of the composition, thus improving its overall mechanical properties.
  • micro-phase separation of the composition is intended to mean the presence or formation of nanometer-sized structures derived from the spatial self-assembly of the composition constituents. Without being confined to theory, such self-assembled structures are believed to form a periodic nanostructured lamellar morphology with connected ion-conducting domains.
  • At least one region of nanophase separation may be characterized by a periodic nanostructured lamellar, hexagonal, 3D continuous or discontinuous morphology. Those domains may extend in one-, two- or three-dimensions throughout the composition.
  • the periodicity of the nanostructured morphology may be characterized by ordered domains having lattice parameter dimensions in the range of about 1 nm to about 500 nm, as measured by small angle X-ray scattering (SAXS).
  • Tg of the electrolyte composition associated with the non-ionic block of the copolymer is not limited to any specific value.
  • Tg of the electrolyte composition associated with the non-ionic block may be between about 30° C. and about 250° C., between about 30° C. and about 200° C., between about 30° C. and about 175° C., between about 30° C. and about 150° C., between about 30° C. and about 125° C., between about 30° C. and about 100° C., between about 40° C. and about 100° C., between about 50° C. and about 100° C., between about 60° C. and about 100° C., or between about 70° C. and about 100° C.
  • Tg of the electrolyte composition associated with the ionic block of the copolymer is not limited to any specific value.
  • Tg of the electrolyte composition associated with the ionic block may be between about ⁇ 100° C. and about 50° C., between, between about ⁇ 100° C. and about 20° C., between about ⁇ 100° C. and about 0° C., between about ⁇ 100° C. and about ⁇ 30° C., between about ⁇ 100° C. and about ⁇ 70° C., or between about ⁇ 100° C. and about ⁇ 90° C.
  • the electrolyte composition has at least two glass transition temperature (Tg) values as measured by Differential Scanning Calorimetry (DSC), the ionic block, lithium species and organic electrolyte may be provided in any relative amount.
  • Tg glass transition temperature
  • the (organic electrolyte:ionic block) molar fraction is between about 0.01 and about 1, between about 0.01 and about 0.9, between about 0.01 and about 0.8, between about 0.01 and about 0.7, between about 0.01 and about 0.6, between about 0.01 and about 0.5, between about 0.01 and about 0.4, between about 0.01 and about 0.3, between about 0.01 and about 0.2, between about 0.01 and about 0.1, or between about 0.01 and about 0.05.
  • the (organic electrolyte:ionic block) molar fraction may be 0.39.
  • the (lithium:ionic block) molar fraction is between about 0.01 and about 15, between about 0.01 and about 12.5, between about 0.01 and about 10, between about 0.01 and about 7.5, between about 0.01 and about 5, between about 0.01 and about 2.5, between about 0.01 and about 1, between about 0.01 and about 0.75, between about 0.01 and about 0.5, between about 0.01 and about 0.1, between about 0.01 and about 0.075, between about 0.01 and about 0.05, or between about 0.01 and about 0.02.
  • the (lithium:ionic block) molar fraction may be selected from 0.00, 0.58, 3.00, and 5.81.
  • the (ionic block:lithium:organic electrolyte) molar ratio is selected from 1.00:0.00:0.33, 1.00:0.00:0.39, 1.00:0.00:0.74, 1.00:0.20:0.21, 1.00:0.46:0.47, 1.00:0.58:0.39, 1.00:1.00:0.00, 1.00:1.01:0.14, 1.00:3.00:0.39, 1.00:5.81:0.00, 1:00:5.81:0.39, 1.00:5.81:0.79, 1.00:5.81:2.36, and 1.00:8.72:1.57.
  • the organic electrolyte comprises organic ionic liquid not covalently coupled to the block copolymer (i.e. free ionic liquid)
  • the ionic block, lithium species and free ionic liquid may be provided in any relative amount provided the electrolyte composition has at least two glass transition temperature (Tg) values as measured by Differential Scanning Calorimetry (DSC).
  • Tg glass transition temperature
  • the (free ionic liquid:ionic block) molar fraction is between about 0.01 and about 1, between about 0.01 and about 0.9, between about 0.01 and about 0.8, between about 0.01 and about 0.7, between about 0.01 and about 0.6, between about 0.01 and about 0.5, between about 0.01 and about 0.4, between about 0.01 and about 0.3, between about 0.01 and about 0.2, between about 0.01 and about 0.1, or between about 0.01 and about 0.05.
  • the (free ionic liquid:ionic block) molar fraction may be 0.39.
  • the (lithium:ionic block) molar fraction is between about 0.01 and about 15, between about 0.01 and about 12.5, between about 0.01 and about 10, between about 0.01 and about 7.5, between about 0.01 and about 5, between about 0.01 and about 2.5, between about 0.01 and about 1, between about 0.01 and about 0.75, between about 0.01 and about 0.5, between about 0.01 and about 0.1, between about 0.01 and about 0.075, between about 0.01 and about 0.05, or between about 0.01 and about 0.02.
  • the (lithium:ionic block) molar fraction may be selected from 0.00, 0.58, 3.00, and 5.81.
  • the (ionic block:lithium:free ionic liquid) molar ratio is selected from 1.00:0.00:0.33, 1.00:0.00:0.39, 1.00:0.00:0.74, 1.00:0.20:0.21, 1.00:0.46:0.47, 1.00:0.58:0.39, 1.00:1.00:0.00, 1.00:1.01:0.14, 1.00:3.00:0.39, 1.00:5.81:0.00, 1:00:5.81:0.39, 1.00:5.81:0.79, 1.00:5.81:2.36, and 1.00:8.72:1.57.
  • the molar weight of the ionic blocks combined with the non-ionic blocks of the copolymer is in itself an effective parameter that can be tuned to assist with the mechanical stability of the electrolyte compositions while maintaining their good ionic conductivity.
  • the molar weight of the ionic blocks combined with the non-ionic blocks of the copolymer is less than about 40,000 g/mol.
  • the molar weight of the non-ionic block combined with the ionic block is less than about 40,000 g/mol.
  • the total molar weight of the non-ionic block and the ionic block may be between about 100 g/mol and about 40,000 g/mol, between about 500 g/mol and about 40,000 g/mol, between about 1,000 g/mol and about 40,000 g/mol, between about 2,500 g/mol and about 40,000 g/mol, between about 5,000 g/mol and about 40,000 g/mol, or between about 10,000 g/mol and about 40,000 g/mol.
  • the amount of organic electrolyte is in itself an effective parameter that can be modified to assist with the ionic conductivity of the electrolyte compositions while maintaining good mechanical stability.
  • it can be particularly advantageous to have compositions in which the organic electrolyte is present in an amount of less than 55 wt. % relative to the total weight of the electrolyte composition.
  • the organic electrolyte is present in an amount of less than 55 wt. % relative to the total weight of the electrolyte composition.
  • an amount of organic electrolyte of less than 55 wt. % relative to the total weight of the composition is believed to ensure that its plasticising effect is minimal, yet it allows for dissolution of a high amount of lithium salt. That in turn is believed to provide for a good balance between high ionic conductivity and mechanical stability of the electrolyte composition.
  • the organic electrolyte in the electrolyte composition is present in an amount of between about 0.1 wt. % and about 50 wt. %, between about 0.1 wt. % and about 40 wt. %, between about 0.1 wt. % and about 20 wt. %, between about 0.1 wt. % and about 5 wt. %, relative to the total weight of the electrolyte composition.
  • the amount of organic ionic liquid not covalently coupled to the block copolymer is in itself an effective parameter that can be modified to assist with the ionic conductivity of the electrolyte compositions while maintaining good mechanical stability.
  • the organic ionic liquid not covalently coupled to the block copolymer is present in an amount of less than 55 wt. % relative to the total weight of the electrolyte composition.
  • an amount of uncoupled ionic liquid of less than 55 wt. % relative to the total weight of the composition is believed to ensure that its plasticising effect is minimal, yet it allows for dissolution of a high amount of lithium salt. That in turn is believed to provide for a good balance between high ionic conductivity and mechanical stability of the electrolyte composition.
  • the organic ionic liquid not covalently coupled to the block copolymer in the electrolyte composition is present in an amount of between about 0.1 wt. % and about 50 wt. %, between about 0.1 wt. % and about 40 wt. %, between about 0.1 wt. % and about 20 wt. %, between about 0.1 wt. % and about 5 wt. %, relative to the total weight of the electrolyte composition.
  • the amount of lithium salt is in itself an effective parameter that can be to assist with the ionic conductivity and lithium transport properties of the electrolyte compositions of the present invention while maintaining their good mechanical stability.
  • the lithium salt is present in an amount of at least 11 wt. % relative to the total weight of the electrolyte composition.
  • the amount of lithium salt may be between about 11 wt. % and about 80 wt. %, between about 11 and 70 wt. % and between about 11 and 60, or between 11 and 55 wt. % relative to the total weight of the electrolyte composition.
  • the ionic conductivity and lithium transport properties of the composition can be improved together with its mechanical stability because the amount of uncoupled ionic liquid, and consequently its plasticising effect, can be minimised.
  • the present invention also provides a lithium-based electrochemical cell, which comprises an electrolyte composition of the kind described herein.
  • the present invention provides a lithium-based electrochemical cell comprising a negative electrode and an electrolyte composition as described herein.
  • the negative electrode may comprise (or be made of), expanded graphite, hard carbon (non-graphitisable carbon), coke, carbon black and glassy carbon.
  • the lithium-based electrochemical cell of the invention supports a current density at the negative electrode of at least 10 ⁇ A/cm 2 , up to a maximum of 2,500 ⁇ A/cm 2 .
  • the lithium based electrochemical cell according to the invention may be configured and used such that electric current flows through the negative electrode along opposite directions in a cyclical manner. This may be achieved by subjecting the cell to polarisation cycles, in which electric current of a certain density flows through the negative electrode along alternating opposite directions. As a result, an electric potential of alternating sign can be observed.
  • a single polarisation cycle is intended to mean a two-step cycle comprising: step 1 in which electric current of a certain density flows through the negative electrode along an initial direction; and step 2 in which the electric current is switched to flow through the negative electrode along the direction opposite to the initial direction.
  • the cell according to the invention can advantageously undergo such polarisation cycles while still maintaining a current density at the negative electrode of at least 10 ⁇ A/cm 2 .
  • a cell undergoing polarisation cycles at a certain current density may also be referred to as being capable of “sustaining” such current density.
  • a charge/discharge cycle may be the charge/discharge performed to activate a rechargeable battery following assembly.
  • this refers to the procedure adopted to form/activate a negative electrode by way of charging/discharging routines under controlled voltage, temperature and environmental conditions, which is performed with the intention of inducing formation of the solid-electrolyte interphase (SEI) layer at the negative electrode.
  • SEI solid-electrolyte interphase
  • the lithium-based electrochemical cell of the invention when undergoing a charge/discharge cycle, has a current density at the negative electrode of at least 10 ⁇ A/cm 2 .
  • the lithium-based electrochemical cell of the invention when undergoing a charge/discharge cycle, has a current density at the negative electrode of at least 10 ⁇ A/cm 2 for at least 10 charge/discharge cycles, or of at least 10 ⁇ A/cm 2 for at least 20 charge/discharge cycles, or of at least 10 ⁇ A/cm 2 for at least 50 charge/discharge cycles, or of at least 10 ⁇ A/cm 2 for at least 100 charge/discharge cycles, or of at least 10 ⁇ A/cm 2 for at least 500 charge/discharge cycles, or of at least 10 ⁇ A/cm 2 for at least 1,000 charge/discharge cycles.
  • the lithium-based electrochemical cell of the invention comprises a positive electrode.
  • a positive electrode refers to the electrode at which electrons enter the cell during discharge.
  • the positive electrode is also commonly referred to in the art as a “cathode”.
  • Examples of material which the positive electrode may comprise (or be made of) include an oxide of a lithiated transition metal such as LiCoO 2 , LiNiO 2 , LiMnO 2 , LiMn 2 O 4 , LiFePO 4 , and corresponding substitutes in which a part of the main metal is substituted by one or more other transition metals such as Co, Mn, Al, Mg, Ti.
  • the positive electrode may also comprise (or be made of) a carbon based-sulphur composite or carbon porous material for Li/sulphur and Li/air (or oxygen) battery, respectively.
  • a lithium-based electrochemical cell of the invention when in a full-cell configuration, may also support a current density at the negative electrode having values described herein.
  • a lithium-based electrochemical cell of the invention when in a full-cell configuration and undergoing polarisation or charge/discharge cycles as described herein, may also support a current density at the negative electrode having values described herein.
  • a full-cell configuration the cell of the invention can advantageously find application as an energy storage device, for example as a lithium-based rechargeable battery.
  • the specific current density that the cell of the invention supports advantageously provides for a lithium rechargeable battery with high discharge capacity and supporting multiple charge-discharge cycles.
  • the present invention also provides a lithium-based rechargeable battery comprising a negative electrode, a positive electrode and an electrolyte composition as described herein.
  • the number of repeating units in the first block was determined by the conversion obtained during polymerisation, while the number of repeating units in the second block was determined by comparing assigned signals of the two blocks in the block copolymer.
  • the polymer's molecular weight, excluding the RAFT moiety, was calculated by adding for each block, the number of repeating units multiplied by the molecular weight of each unit.
  • LiFSI lithium bis(fluorosulfonyl)imide salt
  • LiFSI lithium bis(fluorosulfonyl)imide salt
  • C 3 mpyrFSI N-propyl-N-methylpyrrolidinium bis(fluorosulfonyl)imide ionic liquid
  • the polymer electrolytes were cast on a Teflon mould.
  • the polymer electrolytes were first dried at 50° C. using the argon glovebox antechamber for 24 hours and then further dried at 80° C. under high vacuum using a Schlenk line.
  • S-ImTFSI 64-16
  • RAFT end groups are not included in the molar weight of the S-ImTFSI (DPof S block DP of ImTFSI) calculations.
  • Block copolymer S-ImTFSI N/A 64-16) S-ImTFSI N/A (127-20) S-ImTFSI N/A (127-31) S-ImTFSI N/A (127-73) Block copolymer + S-ImTFSI 1.00:0.00:0.33 C 3 mpyrFSI (64-16) S-ImTFSI 1.00:0.00:0.39 (64-16) S-ImTFSI 1.00:0.00:0.74 (64-16) Block copolymer + S-ImTFSI 1.00:1.00:0.00 LiFSI (64-16) S-ImTFSI 1.00:5.81:0.00 (64-16) Block copolymer + S-ImTFSI 1.00:0.20:0.21 C 3 mpyrFSI + LiFSI (64-16) S-ImTFSI 1.00:0.46:0.47 (64
  • phase behavior and ionic conductivity of the samples were also assessed by differential scanning calorimetry (DSC) and electrochemical impedance spectroscopy (EIS).
  • DSC differential scanning calorimetry
  • EIS electrochemical impedance spectroscopy
  • the T g PIL value for the S-ImTFSI (64-16) is 8.3° C.
  • C 3 mpyrFSI is added to S-ImTFSI (64-16) at a molar ratio of 0.73
  • the resultant T g PIL decreases to ⁇ 33.2° C.
  • the resultant T g PIL is equal to 2.7° C.
  • C 3 mpyrFSI has a more significant plasticizing effect than LiFSI on the PIL phase.
  • FIG. 2 shows ionic conductivity values for S-ImTFSI (64-16) polymer samples with various Li cat /poly cat molar ratio and a fixed IL cat /poly cat molar ratio of 0.39, as well as S-ImTFSI (64-16), at a temperature range of 30-100° C. While the addition of C 3 mpyrFSI to a molar ratio of 0.39 significantly increases ionic conductivity (e.g. 1.68E ⁇ 7 vs. 4.05E ⁇ 6 S ⁇ cm ⁇ 1 at 50° C.), subsequent LiFSI addition have little to no effect on ionic conductivity. Measured values of ionic conductivity for all tested samples are shown in Table 3, below.
  • the morphology of the polymers and their electrolyte compositions were determined by Small-angle X-ray scattering (SAXS).
  • FIG. 4 (A) shows SAXS profiles of the S-ImTFSI (64-16) with various Li cat /poly cat molar ratio (i.e. 0.00, 0.58, 3.00 and 5.81) and a fixed IL cat /poly cat molar ratio of 0.39 as well as S-ImTFSI (64-16), without annealing treatment. All composition presented in
  • FIG. 4 (A) exhibits a lamellar phase, although ordering change are observed.
  • the addition of C 3 mpyrFSI to S-ImTFSI (64-16) results in the formation of a more ordered lamellar phase (i.e. additional Bragg peaks observed).
  • FWHM full width at half maximum
  • FIG. 4 (B) shows SAXS profiles of the S-ImTFSI (64-16) with various Li cat /poly cat molar ratio (i.e. 0.00, 0.58, 3.00 and 5.81) and a fixed IL cat /poly cat molar ratio of 0.39 as well as S-ImTFSI (64-16), with annealing treatment (120° C. for 24 hours). Similar trend than that of the no annealed samples are observed. Although, the use of an additional annealing treatment results in the formation or more ordered lamellar phase, with the exception of S-ImTFSI (64-16) having a poly cat :Li cat :IL cat molar ratio of 1:00:0.58:0.39.
  • FIG. 5 shows SAXS profiles of the S-ImTFSI composites having a poly cat :Li cat :IL cat molar ratio of 1:00:5.81:0.39, with different styrene and PIL degree of polymerization.
  • films made with S-ImTFSI are quite brittle. Films made with S-ImTFSI (127-20) are more robust than the films made with S-ImTFSI (64-16), likely due to the increase of the styrene DP at a given PIL DP. In particular, films made with S-ImTFSI (127-73) are soft and spongy, likely due to the increase of the PIL DP.
  • Lithium transport properties and electrochemical stability of the compositions against lithium metal electrodes were investigated using lithium symmetrical cells that were galvanostatically cycled at various current densities at 50° C.
  • FIG. 6 shows galvanostatic cycling of S-ImTFSI (64-16) compositions having various Li cat /poly cat molar ratio, and specifically (a) 0.58, (b) 3.00 and (c) 5.81) at a fixed IL cat /poly cat molar ratio of 0.39. Although all these compositions exhibit similar conductivity (e.g. ⁇ 7E ⁇ 6 S ⁇ cm ⁇ 1 at 50° C.), significant voltage response difference are observed while cycled Galvano statically from 0.02 mA ⁇ cm ⁇ 2 to 0.2 mA ⁇ cm ⁇ 2 .
  • FIG. 7 shows galvanostatic cycling of S-ImTFSI (127-31) with a poly cat :Li cat :IL cat molar ratio of 1:00:5.81:0.39, from a current density of 0.02 mA ⁇ cm ⁇ 2 to 0.2 mA ⁇ cm ⁇ 2 . Stable overpotential of 0.12 V and 0.25 V for a current density of 0.1 mA ⁇ cm ⁇ 2 and 0.2 mA.cm ⁇ 2 , respectively.
  • Electrochemical tests were also performed in Li metal
  • S-ImTFSI 64-16 was also used as a bifunctional binder for cathode electrode.
  • the full cells were first cycled at a C-rate of C/20 for 1 cycle and then at a C-rate of C/10 for 5 cycles at either 50° C. or 90° C.
  • a slurry of lithium iron phosphate (LFP) based polymer cathode material was prepared by mixing LFP active material (60 wt. %), carbon C65 (10 wt. %) and S-ImTFSI (64-16) as binder (30 wt. %) with a minimum amount of N-Methyl-2-pyrrolidone (NMP).
  • LFP based slurry was casted on A1 current collector.
  • LFP based cathode electrode was pre-dry in air for 24 hours and then further was further dried under high vacuum at 50° C. for 24 hours. The resulted cathode electrode has a LFP loading of 2.1 mg ⁇ cm ⁇ 2 (0.35 mAh.cm ⁇ 2 ).
  • a CE of 99.4% is observed with a charge and discharge capacity of 138 mAh.g ⁇ 1 and 137 mAh.g ⁇ 1 , respectively.
  • a charge and discharge capacity of 137 mAh.g ⁇ 1 and 131 mAh.g ⁇ 1 is obtained, respectively.
  • CE slightly decreases to 96.3%.
  • the charge/discharge capacity and CE remains relatively constant, with a capacity retention of 98.6%.
  • MA-sTFSILi and MA-mTFSILi polymers were made by chain extending polymethylmethacrylate-macroRAFT, with the respective styTFSI.Et3NH and mTFSI.Et3NH monomers using free radical polymerisation, followed by cation exchange of triethylammonium to lithium. Procedures were adapted from (i) J. Li, H. Zhu, X. Wang, M. Armand, D. R. MacFarlane and M. Forsyth, Electrochim. Acta, 2015, 175, 232-239, (ii) L. Porcarelli, A. S. Shaplov, M. Salsamendi, J. R. Nair, Y. S.
  • styTFSI.Et 3 NH monomer was isolated after activation of sodium 4-styrene sulfonate with thionyl chloride, followed by reaction with trifluoromethanesulfonamide under basic conditions.
  • mTFSI.Et 3 NH monomer was similarly obtained, using potassium 3-(methacryloyloxy) propane-1-sulfonate.
  • DMF N,N-dimethylformamide
  • the samples were also characterised by GPC on a Shimadzu system equipped with a CMB-20A controller, a SIL-20A HT autosampler, a LC-20AT tandem pump system, a DGU-20A5 degasser unit, a CTO-20AC column oven, a RID-10A refractive index (RI) detector, and four Styragel HT columns.
  • N,N-Dimethylacetamide (containing 4.3 gL-1 LiBr) was used as the eluent at a flow rate of 1 mLmin ⁇ 1 .
  • the column temperature was set to 80° C. and the temperature at the RI detector was set to 35° C.
  • the GPC columns were calibrated with low dispersity polymethylmethacrylate standards and molar masses are reported as polymethylmethacrylate equivalents. Number (Mn) and mass-average (Mw) molar masses were evaluated using the Shimadzu LC Solution software.
  • a copolymer having a PMMA-based non-ionic block and an butyl-imidazolium-based ionic block was synthesised according to a procedure depicted in FIG. 12 . Specifically, the synthesis was tailored to produce a PMMA-ImTFSI block co-polymer having a (116-32) degree of polymerisation of the two blocks, respectively, to obtain a (poly cat :Li cat :IL cat ) molar ratio of 1:00:5.81:0.39.
  • S-styrene (S)-based copolymer having an ionic block comprising a styrene-TFSI (sTFSI) anionic pendant moiety is shown in the schematic of FIG. 14 .
  • the synthesis procedure was adopted to produce a S-sTFSI with degree of polymerisation of (64-17), respectively. Lithium was used as the counter cation to the pendant sTFSI anion, to obtain a sample named S-sTFSI/Li(64-17).
  • Electrolyte composition A (S-Im/TFSI(64-16))+(Li-TFSI)+(free ionic liquid),
  • Electrolyte composition D (S-sTFSI/Li(64-17))+(Li-TFSI)+(free ionic liquid).
  • Relative (Li:copolymer) and (free ionic liquid:polymer) molar ratios were 2 and 1.5, respectively. All compositions showed two values of Tg measured with DSC, as shown in FIG. 15 . Ionic conductivity data is shown in FIG. 16 .
  • FIG. 17 shows DSC plots measured for samples of the B, C, D and E kind obtained using S-Im/TFSI(64-16) as the copolymer.
  • FIG. 18 shows corresponding ionic conductivity measurement data obtained using samples of the A, B and D obtained using S-Im/TFSI(64-16) as the copolymer.

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